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Aprll 2, 1963
R. M. MCGLAMERY
3,083,410
COLD ROLLING FILM OF HIGH DENSITY ETHYLENE POLYMER
Filed NOV. 23, 1956
Ä TTORNEVS.
United States Patent() ”
i
3,083,410
CGLD ROLLING FILM ÜF MGH DENSITY
ETHYLENE >Piltl'uiflidlE-R
Roger M. Me'Glamery, Bartlesville, -Ülrla., assigner to
Phillips Petroleum Company, `a corporation of 'Deia
Ware
CC
3,083,410
Patented Apr.. 2, 1963
2
240° F. The ethylene homopoly'mer has a softening tem
perature in the range of Z50-270° F., usually about 260°
F., but this is generally depressed -by the incorporation of
higher molecular weight comonomers. Although Vthe
ethylene homopolymer is preferred-by reason-»of its higher
softening temperature, monoolelins of from 5-12 carbon
Filed Nov. 23, i955, Ser. Bla-623,775
6 Claims. (Cl. 18-48)
atoms are .suitable >as comonomers in amounts up to ¿3
relates to a method of increasing the tensile strength and
cent of the total polymerizable material and still retain
weight percent of the total polymerizable material. .The
lower molecular weight monoolefins, for example, pro
This invention relates to a method of making an im 10 pylene, l-butene and 2-butene or mixtures thereof, can
proved film from ethylene polymers. Inanother aspect it
be used as comonomers in amounts up .to Al5 yweight per
improving other physical properties of ethylene polymer
satisfactory properties in the finished Ypolymer suitable
ñlrns by cold rolling.
for the practice of my invention.
Improved methods of polymerizing ethylene and other 15
These polymers are generally regarded as having a
monooleñns have been developed whichproduce ethylene
high degree of crystallinity as determined by nuclear mag
polymers having a relatively high tensile strength when
shaped into lfilms or fibers. These ethylene polymers can
netic resonance, generally at least 70 „percent at 25° C.
and preferably'SO percent and above.
be distinguished from commercial type polyethylenes
These-polymers likewise have a characteristic high soft
produced by processes employing high temperatures »and 20 ening temperature as discussed above. By “softening tem
pressures by their normally higher densities, softening
perature” as used in this specification, I refer to the ability
temperatures and crystallinity.
of the polymer to support a standard load or withstand »a
I have discovered a method of improving still further
force at elevated temperatures without substantial de
the tensile strength and other physical properties of these
formation. “Softness” of a polymer is a measure of its
higher softening ethylene polymers by cold rolling to pro 25 relative deformation under a .standard -load for a certain
duce a film of any desired thickness. I have found ‘that
a quite unexpected increase in tensile strength can «be
effected for films prepared from these more crystalline
time interval at a particular temperature. The method
for determining softness as used in this specification is
that described in the article `by Karrer, Davis, and
ethylene polymers by -a severemilling step at temperatures
Dieterich in Industrial and Engineering Chemistry (Ana
below the softening point of said polymers so that a high 30 lytical Edition) 2, 96 `(1930). The softening temperature
percentage reduction in thickness of the initial stock >is
for apolymer is determined by plotting softness over a
obtained. I have further discovered that these more
range of temperatures with temperature on the abscissa.
crystalline ethylene polymers will withstand such a severe
As softness increases with temperature, the slope of the
cold rolling >much more readily than »will polymers of
curve formed by the plot likewise increases 'and the tem
the lower softening commercial type. Improvements in 35 perature at which the slope of the curve equals the tangent
tensile strength and haze reduction far beyond what would
of 60° is, by definition, the softening temperature.
normally be expected >can be realized by cold rolling
A method of producing these polymers is by poly
these ethylene polymers in two directions or by other
merizing ethylene with Vor ‘without comonomers in the
wise effecting a'biaxial orientation thereof.
presence of a catalyst comprising chromium, aportion of
It is an object of my invention to provide a method for 40 which is hexavalent (preferably at least 0.1 weight per
producing improved films, tapes, ribbons, and the like
cent of the total catalyst) as chromium oxide associated
Vfrom high-density ethylene polymers. It is another object
with at least one oxide from the group consisting of silica,
of my invention to yprovide a method of improving the
alumina, zirconia, and thorai. The total chromium con
tensile strength of such polymeric ñlms by cold rolling.
tent of the catalyst is preferably between 0.1 and l0
It is still Vanother object of my invention to improve the -45 weight percent. Polymerization is ordinarily carried out
tensile strength and clarity of such polymeric films by
at a temperature between 150 and 450° F. and the pres
biaxial orientation. A further object is to provide a
sure of the reaction can vary over a wide range, for eX
method of increasing -tensile strength of polymeric films
ample, from atmospheric pressure to 1,000 pounds .per
by a single-pass calendering at approximately’ room tem
square inch absolute. However, generally this reaction
perature. Other objects and advantages and features will 50 is known as low pressure polymerization. The reaction
be apparent to those skilled in the art from the following
can be carried out in a gaseous phase; but with the use
discussion, examples and drawing in which:
of a diluent, as preferred, the minimum pressure is that
FIGURE 1 is a schematic ñoW diagram of the com
necessary to maintain the diluent in la liquid phase. The
plete process, including polymerization, polymer recovery,
diluent may be any solvent which is liquid and inert under
molding and cold rolling;
55 contacting conditions, such as hydrocarbon solvents, espe
FIGURE 2 is an enlarged View of the cold rolling step
cially naphthenic hydrocarbons and paramnic hydrocar
shown in FIGURE l; and
bons of from 3-12 carbon atoms, for example, normal
FIGURE 3 is'a diagram Vshowing the biaxial cold roll
pentane, isopentan'e, isooctane, cyclohexene and methyl
ing process for a slab of polymeric material.
cyclohexane. In such cases the reaction pressure is ordi
The polymers to which my invention applies are poly
narily in the range of about 10U-800 pounds per square
inch absolute.
mers of ethylene with or without minor amounts of other
acyclic monooleiins prepared by processes using relatively
The eiiiuent Áwithdrawn from the reactor ordinarily
comprises a solution of polymer in solvent and when a
low temperatures and pressures. The polymers which are
applicable have a density of about 0.94 and above, prefer 65 slurry or suspended catalyst is used, the eiiiuent also
contains catalyst. Unreacted monomers are removed
erably above 0.955. These polymers have a melt index of
by dashing, and the etiiuent with or without the addition
lgenerally not over 20 and preferably in the order of l
of more solvent is filtered, centrifuged or the like to re
to 5 and below, with a softening temperature of at least
move the catalyst. The catalyst-free solution is then
3,0%,410
3
passed to suitable recovery steps lfor removal of the sol
vent, such as by evaporation or flashing, and the solid
polymer is recovered in these steps or by precipitation.
The catalyst-removal setup is optional and for some appli
cations catalyst can be allowed to remain in `the polymer.
The solid polymer is ordinarily processed further in order
to be placed in condition for storage. Pellets or granules
are a suitable form and -these can «be prepared by extrud
ing the polymer into strands which are then cut or
chopped in a pelletizer.
Preparation of such polyoleñns is more fully ‘described
in the copending application of Hogan and Banks, Serial
When the ñltration step is used, solvent and polymer
leave through line 2@ and the catalyst is removed from the
filtration equipment Iby a flushing solvent entering by line
2l and leaving through line 22. Solvent is removed from
the polymer in solvent evaporation step 23, the solvent
vapors being removed overhead through line 24 and rc
covered for reuse in the process. Polymer passes through
line 26 to an extrusion pelletizing step 27 which places
the polymer' in condition for storage, shipping or molding.
Polymer pellets thus formed pass by conduit 2S to ex
truder 'hopper 29 of extruder Si?. Hopper 29 is heated
by steam jacket ‘31 so that the polymer is heated above
2,825,721.
its softening temperature to a fluid state which can be
readily molded into a tape or film. Extruded tape 32
leaves the extruder 30 and is cooled in the air space and
suitable method is a low temperature, low pressure process
water Vbath 33 into which cooling water enters by line
34 «and leaves through line 36. Tape 37 thus cooled be
low its softening temperature is passed through rolls I38
and 39 which `effect the cold rolling step above described.
No. 573,877, «tiled on March 26, 1956, now Patent No.
While the above described process is the preferred man
ner of preparing »the polymers for rny invention, any proc
ess which will yield a polymer having the required physi
cal characteristics is satisfactory. For example, another
in which the polymerization is effected in 4the presence 20 The cold rolling is severe enough to effect a reduction
in thickness of the polymer tape of at least about 60
of catalyst systems which preferably comprise an organo
percent. The cold rolled ‘tape 40, which has greatly
metal derivative as one component. Such catalyst com
increased tensile strength, is Wound upon a spool 41
positions can have two or more components, one compo
which rotates at a speed required to take up the extra
nent being an organometal compound, metal hydride, or
length of tape which is formed as a result of the roll
a group I, Il, or Ill metal and the other component being
down
by rolls 3d and 39. An enlarged view of the cold
¿a compound of a group IV to Vi metal. Wit-h certain
rolling step is shown in FIGURE 2 in which the cooled
of the above two component systems, an organic halide
tape 37 passes through rolls 38 and 39 to form the cold
having 30 of less carbon atoms per molecule or a metal
rolled tape 4€? of greatly reduced thickness.
halide can be used advantageously as a third catalyst com
ponent. Specific examples of suitable catalyst systems 30 While advantages cari be gained by calendering in a
single direction, further improvements in tensile strength
are triethylaluminum and titanium tetrachloride, mix
and film clarity can çbe realized by -biaxial cold rolling.
tures of ethylaluminum halides and titanium tetrachloride,
This is done by iirst calendering the polymer stock in
titanium tetrachloride and sodium or manganese, and
one direction and then passing the material through the
titanium tetrachloride with lithium aluminum hydride and
85 roll mills so that cold rolling will be eñected in a direc
ethyl bromide.
tion 90° to the original direction. To put it another Way,
In preparing the íilms for my invention the polymer
the polymer stock is cold rolled in a first direction and
must `first be shaped into a form which is suitable for
calendering or cold working on a roll mill. For this pur
pose the polymer can be shaped »into a slab, sheet, or the
like -by any or“ a number of operations suitable for work
ing the polymer while above its softening point, for ex
ample, by «compression molding, injection molding or ex
trusion. A polymericV material thus formed into a slab,
sheet, tape, ribbon, or the like is cooled below »its soften
secondly in a ltransverse direction.
Such a treatment
effectsra biaxial orientation and produces many desirable
results such as -increased tensile strength, reduced haze,
decreased modulus of elasticity and a considerably reduced
flex temperature. Films produced by the method de
scribed have a smooth, flat surface in sharp contrast to
the commercial polyethylenes processed under compar
ing temperature and processed by cold rolling in a roll 45 able cold rolling conditions.
FIGURE 3 shows an isometric view :of the biaxial cold
mill.
rolling
step in which a slab of polymer is cold rolled
The temperature at which this calendering operation
ñrst in longitudinal direction and then in a transverse
is effected can vary over a wide range, the upper temper
direction. Slab of polymer' 42 is passed through rolls 43
ature being substantially below, for example, about l0 to
and
44 `to eíect a reduction of thickness at at least about
15° below the softening point of the polymer. Although 50
60 percent and product slab 46. Slab 46 coming from
the cold working operation can be effected quite satis
rolls 43 .and 44- hits stop 47 and is moved at right angles
factorily within a temperature range of about l0() to 175 °
by conveyors not shown through rolls 48 `and 49 which
F., it is preferred to operate at about room temperature for
cold roll the slab in a direction at right angles to the
convenience, economy and ease of control. The setting of
the roll mills should be such as to eñect a substantial re 55 cold rolling performed by rolls ‘43 and 44. The end
duction in 'thickness of the polymer stock on a single pass
through the mills.V To realize full advantage of rny inven
tion, this thickness reduction per pass should be at least
about 50 percent and preferably above about 60 percent.
In other words, the degree of roll-down per pass in order 60
to eiiect marked improvements in tensile streng-th should
be such that the final thickness is not greater than 50
product is a slab of polymer Sil which has improved ten
sile strength in both its longitudinal and transverse direc
«tions and has a thickness of not over 40% of slab 46.
To further clarify the processes of my invention, the
following examples are presented.
EXAMPLE I
Ethylene was polymerized in a continuous process in
a 60-gallon reactor equipped with a stirrer in the pres
percenaand preferably not greater than 40 percent, of
the original thickness.
ence of a chromia-silica-alumina catalyst. Reaction con
Referring to FÍGURE l of the `drawing for a further 65
ditions were as follows:
description of the process, feed streams of ethylene,
Temperature, ° P ___________________________ __ 279
diluent and catalyst are introduced through lines liti, 1l
Pressure, pounds per square inch gage __________ __ 420
»and 12 respectively into polymerization reactor i3 Where
Catalyst concentration in reactor, Weight percent____ 0.4
in polyethylene is formed having «the essential character
Iistics above described. Reactor effluent îlows through 70 Polymer concentration in reactor, Weight percent-“ 9.0
ethylene is removed through line ‘17 for reuse in the proc
Chromium (as Ichromium oxide)
weight percent
ess. v Polymer, solvent and catalyst pass through line 13
Cyclohexane feed rate, pounds per hou-r ________ __ 121
to catalyst tiltration step 19, which is an optional step
Ethylene feed rate, standard cubic feet per hour____ 272
as vthe catalyst can -be allowed to remain in the polymer.
Residence time, hours _______________________ __
line 14 to monomer flashing zone i6 where unreactcd
in catalyst,
2.5
2.9
3,083,410
5
6
After separation of catalyst and solvent a polymer
and percent reduction in thickness.
product was recovered having the following properties:
Density _
__
__
0.961
Crystallinefreezing point °.F.1 _____________ __
252
Melt .index2 ____________________________ __
0.65
Injection molded:3
on four samples are shown in Table yII.
Table II
Tensile, pounds .per square inch ________ __
4600
Elongation, percent4 _________________ __
60
Tensile, pounds per square inch ________ __
4545 10
Compression molded:
Elongation,
.percent __________________ __
20
1
2
3
120
150
_
350
155
170
233
216
400
Second direction_____
66
.100
200
.193
On first pass _______ __
0n second pass 1 _______________ __
70
40
68
67
80
67
Roll temperature, ° F ______________ __
Extension on calender, percen
First direction _________ __
Thickness reduction, percen
'Impact strength, .Izod 5 ____________________ __
4.25
Crystallinity at 25° C., percent 6 ____________ __
>92
Softening temperature, ° F. ’l __________ __-_____ 260i2
Tensìiìle
strengthLpounds per square
mc :
First dire
Second d
1*Determined
melting“
point. on a cooling curve; frequently designated as
10, 970
9, 220
Elongation, percent
First direction
3 ASTM D638-52T.
Second directi
4 ASTM M12-51T.
5 ASTM 13256-47'1‘.
Tear, grams ‘per mil:
20
fAs determined by nuclear magnetic resonance.
Rolling was done
in both directions as described in the preceding example.
The oriented iilms‘had smooth, regular surface. Results
ADetermined as described in the discussion above.
_
____________ __
First direction _________________ __
Sheets were prepared by cold -calendering compression
molded slabs-ofthe ethylene polymer. The work was
'
17, 500
4, 450
8, 250
4,960
f
12, 230
6, 875
70
53
183
»G0
420
435
380
190
770
Second directionDensity ____________________________ __
78
50.
4
850
760
454
286
323
364
»248
0. 946
6. 949
v0. 950
...... __
l Based on thickness 0i reduced stock after first pass.
The above data show ïthat improvements in tensile
done on a Bolling threefroll calender which was operated
at room 'temperature v(6d-86° FZ). The rolls were 8 25 vstrength Vcan nbe realized -by biaxial'rolling over a rela
tively broad ’temperature range below the softening tem
inches in diameter and they Were run at -a speed of 11
peratureof lthe polymer.
revolutions per minute. The amount of mechanical treat
ment is expressed as -pcrcent extension `in Vthe direction
EXAMPLE III
of rollin-g and percent reduction «in thickness. Rolling 30
Compression molded slabs of the `ethylene polymer
was done in both directions, i.e., at `90 degree angles to
described in Example I, 0.060 inch 'in thickness, were
each other. A single pass of the material was made
~formed into 'sheets'by cold rolling on :a small dilîerenti'al
through »the `calender in each direction. Results on five
roll mill.
samples of different thickness and on a sample which
was not calendered (sample 6) are shown in Table I.
Table I
1
2
3
4
5
The mill rolls were operated at room tem
perature with a single pass of the kmaterial --being made
through the mill-in each direction. The following data
show the decrease in llex temperature and modulus of
elasticity as a result of the cold rolling treatment:
Table III
6
40
‘Initial stock thickness,
inches _______________ __ O. 036
Extension on calender,
Treated
by >cold
'
0.050
0.065
0.120
0 190
0 065
____ __
rolling
percent:
First direction ..... __
83. 3
A200
183
233
233
Second direction_____
Thickness re duction ,
83. 3
S3
100
233
233 ____ __
On first pass _______ __
45
On second pass 1_____
67
65
70
45
45
50
70
per square inch:
First direction _____ __ 5, 220
6, 623
11, 600
8, 216
4, S93
4, 620
6, 040
Tensile strength, pounds
70
70 ____ __
First direction__
_
246
v117
70
143
57
20
_
330
240
413
137
267
____ __
740
____ __
irst direction
Second direct;
_
640
v
~33
______________ __
33
On iìrst pass __________________________ __
On second pass 1v ________ __* ______________ __
25
25
'770
875
720
680
570
350
630
_ 0.955
0.956
0. 94S
0.951
First direction ___________________ __
Second direction ________________ __
4, 541
Second direction
Density__
_
Tensile strength, pounds per square inch:
13, 966
_ 5, 483
Tear, grams per 1n
First direction ___________________________ __
' Second direction____
Thickness reduction, percent:
____ _
Second direction
Elongation, percent:
Extension on roll mill, percent:
45
percent:
, 713 ____ __
4, 493
4, 720
50 Elongation, percent:
First direction _______________ __
100
20
42
__________ __
Second direction ____________ __
Modulus of elasticity:
,
First direction _________ __
Second direction_ _
Flex temperature, °
376 ____ __
0. 945
Control
0.961
55
_
42,1000
155, 000
52, 500
__________ __
_
.First direction
Second
direction_
-20
_ _ _ _ _ _
_ _ _ _ __
-l
+70
__________ __
l Based on thickness of reduced stock alter first pass.
Substantial reductions in haze are obtained as are
1¿Based on thickness of reduced stock after ñrst pass.
sult of the calendering treatment. Each of the oriented
The data of this yexample Idemonstrate that physical
films had a smooth, regular surface. The percent thick 60 properties other than tensile strength can ‘he modilied'by
ness reduction in Table I vand the data of'the other ex
a comparatively mild cold rolling treatment.
amples is an overall reduction calculated from the meas
EXAMPLE |lV
_
ured extension of the stock upon calendering. The `in
crease in tensile strength for the high density ethylene
The transparency of arñlm of the ethylene polymer
polymer upon biaxial cold rolling is well shown by the 65 described in Example l, produced by biaxial rolling was
above data, particularly when the percent reduction in.
compared with a compression molded sample of the
thickness is above about 50 percent.
EXAMPLE «II
>same thickness.
The results were -as follows:
Table 1V
Compression molded -slabs of the ethylene polymer 70
described in Example I, 0.065 inch in thickness, Were
formed into sheets -by cold calendering on a Bolling three
roll calender operated at temperatures varying from 120
to 170° F. The amount of mechanical treatment is ex
pressed as percent ,extension in the direction of rolling 75
Thickness, inches _______________________ __
Haze, percent ___________________________ __
Biaxially
Compres~
rolled film
sion molded
0. 004
27. 7
0. 064
68
accanto
7
8
on a continuous basis in a 60-gallon reactor equipped with
a stirrer. Reaction conditions were as follows:
The improvement in film clarity ettected by the proc
ess of my invention is quite evident ¿from the above data.
Temperature ° F
EXAMPLE V
302
Pressure, pounds per square inch gage__.____i_'_____ 420
Catalyst concentration in reactor, lweight percent___ 0.07
-Polymer concentration in reactor, Weight percent-- 8.0
Compression molded slabs of the ethylene polymer
described in Example i, 0.060 inch in thickness, were
Chromium (as chromium oxide) in catalyst, weight
’ formed into sheets by coldv rolling 0n `a differential roll
percent
mill. The mill rolls were operatedVV at room temperature
(around 68-86" E). The rollswere seven inches in
length and three inches in diameter.V The back roll was
operated at 32 revolutions per Vminute and the front roll
at 30 revolutions per minute. The amount of rolling is
____
-
_
2.5
Cyclohexane feed rate, pounds per hour _________ __ 200
Ethylene feed rate, pounds per hour__.____l ______ __ 30
Residence time, hours _______________________ __
1.7
Following separation of catalyst and solvent a polymer
was recovered having the following properties:
expressed `as percent extension in the -direction of the
rolling and the thickness reduction is a calculated aver
age reduction based on the extension. Rolling was done
in the manner described in the preceding examples with
the exception that a single pass ot the material was made
through the roll mill in oneV direction only. The sur
Volatiles, Weight percent __________________ __
0.03
Ash, weight percent _______________ __. ______ __
0.00
Crystalline freezing point, ° El _____________ __ 253:4;2
Density
Melt
___
__
0.961
index2 _______________ -_i ____________ __
0.76
vfaces of the calendered sheets were smooth and regu 20 Injection molded: 3
lar. The results are shown in Table V.
Tensile, pounds per square inch _________ __
4624
~Elongation,
Table V
percent __________ __' ______ __
33
Compression molded: ‘1 »
1
2
3
4
5
Tensile, pounds per square inch ________ __
4536
Elongation, percent __________________ __
20
Impact strength, Izod, foot pounds per inch
Extension, percent ______________ __
39
65
90
125
_ 0
Thickness reduction, percent ____ -_
28
30
47
55
72
notch5
Tensile strength, pounds per
square inch ___________________ __ 4,840
Elongation, percent _____________ __
50,50
5, 400
6,250
8,250
70
Y75
230
105
60
___
3.4
Heat distortion, ° Fß. _______________________ __
_
.
-_
171
Stitîness, pounds per square inch '7____ ______ __ 153,300
>92
30 Crystallinity at 25° C., percent 3 ____________ __
Sottening temperature, ° R9 ______________ __
260i2
1 Frequently designated as melting point; determined on a
cooling curve.
As shown by the above data, a given percent reduction
in thickness above about 50 percent reduction produces «a
proportionally greater increase in tensile strength than a 35
2 ASTM D1238-52T.
t ASTM D41 2-51T.
corresponding percentage reduction below 50 percent.
'J ASTM 13648-4502'.
7 ASTM DHT-50.
EXAMPLE VI
SAS determined by nuclear magnetic resonance.
9 Determined as described lin the discussion above.
A sample of commercial polyethylene (Bakelite 40 Polyethylene B was a commercially available polyethyl
DYNH) had the following properties:
ene sample prepared by a low pressure process employing
an organometallic catalyst. This polyethylene had a den
Melting point, ° F _______________ ___-; ____ __ 2.10-214
Density
________ __. ___________ ____.____.__.__
Molecular weight
0.92
21,000
Tensile strength, pounds per square inch ______
1,800
Elongation, percent ___________________ ____
550
Crystallinity at 25° C., percent.......__.______
65
sity of 0.951 and crystallinity of 82 percent. Polyethyl
v eue C, prepared by the high pressure process, had a den
sity of 0.92 and a crystallinity of 65 percent.
Several samples of polyethylene C were tested to deter
mine the approximate maximum reduction possible for
this material at room temperature. The resultsof these
tests are shown in Table VI. The roll temperature for
-A compression molded slab of the commercial poly
ethylene, 0.060 inch in thickness, was-cold rolled on a 50. each run was maintained at labout 78° F.
Table Vl
seven-inch differential roll mill Voper-ated in the manner
described in Example V. On the tirs't pass the slab was
reduced in thickness -by 43 Vpercent and on the second pass
Poly- PolyPolyethylene C, samples
cthyl~ ethyl
in the transverse direction by 60 percent based on the
ene A ene B
1
2
3
«t
thickness of the reduced stock. A til-m was produced 55
having a surface that was irregular in thickness as evi
denced by bulging of the center and puckering of the
edges. Numerous fissures were evidenced throughout the
iilm. These were produced by shredding of the material
as it .passed through the roll mill. |Thus, it is evident that 80
commercial polyethylene does not withstand extreme cold
working processes as Well as the higher crystalline poly
mers employed for my invention.
EXAMPLE VII
Samples of polyethylenes produced by three diiiïerent
processes were compared to determine their ability to with
stand severe cold .Working processes. The polyethylenes
compared were polyethylene A, prepared 4as described be
_ loW in the presence of a chromium oxide-containing cata
lyst; polyethylene B, arhighly crystalline polymer .pre
pared in the presence of an organometallic catalyst; and
.polyethylene C, `a commercial polyethylene (DYNH)
substantially the same as that used in Example VI.
Initial thickness ...... __
Final thickness _______ __
0. 119
0.022
0.119
0.020
0.110
0. 032
0.119
0. 04B
0.110
0.050
0.119
0.078
Thickness reduction,
percent _____________ __
Appearance __________ ._
1 Smooth.
S2
(i)
83
(l)
73
(2)
2 Rough and discontinuous.
60
(3)
58
(l)
3i
(l)
3 Slightly rough.
The above examples can -be summarized as follows: As
shown by Examples 1I and I‘I, biaxially rolled highly crys
65 talline ethylene polymer has greatly improved tensile
strength, especially when a substantial thickness reduction
is effected in each pass through the rolls. lExample lll
shows quite Well that other physical properties can be
improved for particular applications by cold rolling these
polymers biaxially, even with somewhat lesser reduction
in thickness. Modulus of elasticity is considerably re
duced and the flex temperature of the biaxially rolled film
is much lower. .Example IV shows the remarkable im
provement in tensile strength and clarity of the ñlm
Polyethylene A was prepared by polymerizing ethylene 75 etl‘ected by biaxial rolling.
8,083,410
The data of Example V show that considerable tensile
strength improvement is gained by cold `rolling in a sin~
gle pass between rolls in a second direction at right angles
to said Íirst direction at a temperature below the softening
temperature of said polymer to effect a reduction in thick
ness of the sheet rolled in said ñrst direction above 60
gle direction with a reduction in thickness per pass above
about 50 percent. Examples VI and VII demonstrate
quite markedly the unexpected advantage of the higher
percent the improvement which comprises employing as
said polymer an ethylene polymer characterized by a den
sity of at least 0.94, a softening temperature of at least
crystalline polyethylene over the less crystalline commer
cial polymer to withstand extreme cold working processes
and thereby realize the tensile strength improvements
240° 1F. and a crystallinity at 25° C. or" at least 80 percent,
which the process of my invention imparts.
said ethylene polymer being a polymerizate of a mono
The above examples are presented for exemplary pur 10 rner system containing 85 to 100 Weight percent ethylene,
poses only and should not be interpreted as limiting my
O to l5 weight percent monoole?in selected from the group
invention unduly.
consisting of propylene, 1-butene and 2-butene, and Oto 3
I claim:
weight percent acyclic monooleñn having 5 to 12 carbon
l. In a cold rolling process wherein a sheet of thermo
atoms per molecule.
plastic polymer makes a single pass between rolls at a tem 15
4. A method according to claim 1 wherein said poly
perature below the softening temperature of said polymer
mer is polyethylene characterized by a density of at least
to effect a reduction in thickness of said sheet above 60
0.955, a softening temperature of at least 250° F. and a
percent the improvement which comprises employing as
crystallinity at 25° C. of at least 90 percent.
said polymer an ethylene polymer characterized by a den
5. A method according to claim 1 wherein said cold
sity of at least 0.94, a softening temperature of at least 20 rolling step is performed at about normal room tempera
240° F. and a crystallinity at 25° C. of at least 80 percent,
said ethylene polymer being a polymerizate of a monomer
system containing 85 to 100 weight percent ethylene, 0 to
l5 Weight percent monooleiin selected from the group
ture.
6. A method according to claim 3 wherein said poly
mer is polyethylene characterized by a density of at least
0.955, a softening temperature of 250° F., and a crystal
consisting of propylene, 1-butene and 2-‘butene, and 0 to 25 linity at 25° C. of at least 90 percent.
3 weight percent acyclic monooleiin having 5 to 12 car
bon atoms per molecule.
References Cited in the tile of this patent
2. A method according to claim 1 wherein said poly
UNITED STATES PATENTS
mer is a copolymer of ethylene and l-butene.
3. In a cold rolling process wherein a sheet of thermo
plastic polymer makes a single pass between rolls in a
first direction at a temperature below the softening tem
perature of said polymer to eiîect a reduction in thickness
oi' said sheet above 60 percent and thereafter makes a sin
30
1,908,546
Sheppard et al _________ __ May 9, 1933
2,244,208
2,406,127
Miles _______________ __ June 3, 1941
Alfthan ____________ __ Aug. 20, 1946
510,145
Canada _____________ __ Feb. 15, 1955
FOREIGN PATENTS